JP5840310B1 - Copper alloy sheet, connector, and method for producing copper alloy sheet - Google Patents

Abstract

High electrical conductivity and high strength copper alloy plate material in any direction of 0 ?, 45? Or 90? Direction from the rolling direction to the vertical direction of rolling, a connector using the same, and the copper alloy plate material A manufacturing method is provided. One or two of Ni and Co in total 1.80 to 8.00 mass%, Si 0.40 to 2.00 mass%, and Sn, Zn, Ag, Mn, P, Mg, Cr , Zr, Fe, and Ti at least one element selected from the group consisting of 0.000 to 2.000 mass% in total, the balance is composed of copper and inevitable impurities, and the conductivity is 20 to Copper alloy plate material of 40% IACS or more and tensile strength in the direction of 0 ?, 45 ?, 90? From the rolling direction to the rolling vertical direction is 1020 to 1400 MPa, a connector using the same, and its copper alloy A method for manufacturing a plate material.

Description

  The present invention relates to a copper alloy sheet, a connector using the same, and a method for producing the copper alloy sheet.

  Terminals and connectors for connecting electronic devices to external devices and the like are required to be further miniaturized as electronic devices become smaller and thinner. In addition, since these terminals and connectors may be inserted and removed and fitted several times a day, the strength and fatigue resistance characteristics (repetitive characteristics) of the spring portion are also required. Since terminals and connectors require strength and conductivity, they are often manufactured using a copper alloy. Therefore, a copper alloy material for a terminal / connector that can be compactly formed and has excellent strength and fatigue resistance is desired.

  In particular, the terminals and connectors are manufactured by punching a copper alloy plate and press-molding it. At this time, the stress load direction of the spring portion of the terminal or the connector is 90 ° or 45 ° from the rolling direction (RD; Rolling Direction) of the copper alloy sheet to the vertical direction of rolling (TD; Transverse Direction). There are many cases. For this reason, the copper alloy plate material for terminals and connectors is required to have excellent fatigue resistance in any of these directions. Further, when the length of the spring portion is shortened with the miniaturization of the terminal and the connector, the stress applied to the spring portion is increased. For this reason, the copper alloy sheet is required to be hard to be permanently deformed even when a high stress is applied in addition to the good fatigue resistance.

  Conventionally, phosphor bronze has been most frequently used as a copper alloy for springs. Phosphor bronze copper alloys for springs are excellent in strength and fatigue resistance, but have a conductivity as low as around 10% IACS. For this reason, it is considered that the use of phosphor bronze-based spring copper alloys may be restricted for future terminals that are small and require high reliability. This is because a spring material for terminals that is small and requires high reliability is required to have a conductivity of 20% IACS or more.

  Cu-Ni-Si copper alloys, so-called Corson alloys, are alloys that have been developed for lead frames and are also used for connectors. Conventional Corson alloys have better electrical conductivity than phosphor bronze alloys. However, conventional Corson-based alloys sometimes do not satisfy recent demands in terms of strength and fatigue resistance. In particular, the fatigue resistance in the direction of 45 ° or 90 ° was inferior even in the direction of 0 ° from the rolling direction to the vertical direction of the rolling (that is, the rolling direction) even though the properties were good.

  Due to such technical trends in electronic equipment, a material having high electrical conductivity and excellent strength and fatigue resistance in any direction of 0 °, 45 ° or 90 ° from the rolling direction to the vertical direction of rolling is required. It is said that.

In Patent Document 1, an alloy composition including a Cu-Ni-Sn alloy-containing component is selected, and a copper alloy with good fatigue characteristics is obtained without decreasing the conductivity by aging precipitation hardening in a specific process. It has been proposed to do.
Patent Document 2 proposes adjusting the crystal grain size and finish rolling conditions of a Cu-Sn alloy to obtain a high-strength copper alloy.
In Patent Document 3, it is proposed that when the Ni concentration is high among Cu-Ni-Si-based alloys, the strength is increased by preparing in a specific process.
Patent Document 4 proposes selecting an alloy composition containing a Cu-Ti alloy-containing component and increasing the strength by age-precipitation hardening in a specific process.

In Patent Document 5, Cu-Ni-Si-based alloy strips are obtained in a specific manufacturing process, thereby having a predetermined {110} <001> orientation density and a KAM (Carnel Average Misorientation) value, and deep drawing workability. It has been proposed to improve fatigue resistance.
In Patent Document 6, the difference between the three tensile strengths, that is, the tensile strength in the rolling direction, the tensile strength in the direction of 45 ° with respect to the rolling direction, and the tensile strength in the direction of 90 ° with respect to the rolling direction. A Cu-Ni-Si-based copper-based precipitation type alloy sheet for a contact material having a maximum value of 100 MPa or less has been proposed.
In Patent Document 7, it is possible to improve bending workability, stress relaxation resistance, and fatigue resistance with high strength by appropriately controlling the area ratio of the Cube orientation and BR orientation of the Cu—Ni—Si based alloy. Proposed.

Japanese Unexamined Patent Publication No. Sho 63-312937 JP 2002-294367 A JP 2006-152392 A JP 2011-132594 A JP2012-122114A JP 2008-095186 A JP 2012-246549 A

By the way, in patent documents 1-4, although compared with the general copper alloy, although high intensity | strength was acquired, depending on the alloy type | system | group and the manufacturing method, the electrical conductivity might still be low.
In Patent Document 5, although deep drawing workability and fatigue resistance characteristics are obtained, there is still room for improvement in terms of strength and conductivity.
In Patent Document 6, although high electrical conductivity is obtained, there is still room for improvement in terms of compatibility with high strength.
In Patent Document 7, although bending workability, stress relaxation resistance, and fatigue resistance are obtained, there is still room for improvement in terms of achieving both high strength and high electrical conductivity.
Moreover, in these patent documents 1-7, it is not paying attention to making it high intensity | strength in any direction of 0 degree, 45 degrees, or 90 degrees toward a rolling perpendicular direction from a rolling direction, and actually any of these directions However, it is unclear whether the tensile strength is high.
Accordingly, there is a demand for a copper alloy sheet material having good electrical conductivity and high tensile strength in any direction of 0 °, 45 ° or 90 ° from the rolling direction to the vertical direction of rolling.

  In view of the above problems in the prior art, the object of the present invention is high conductivity and high strength in any direction of 0 °, 45 ° or 90 ° from the rolling direction to the rolling vertical direction. It is preferable to provide a copper alloy sheet material that is also excellent in fatigue resistance in any direction. Moreover, it is providing the connector using this copper alloy board | plate material, and the manufacturing method of this copper alloy board | plate material. In particular, the present invention provides a copper alloy plate suitable for a thin spring material for a camera module, a movable piece of a relay, and a connector using the same, as well as an external connection connector represented by a dock connector or a USB connector, and a copper thereof. It is an object to provide a method for producing an alloy sheet.

  As a result of intensive studies to solve the above problems, the present inventor has a specific Cu- (Ni, Co) -Si-based alloy composition, and a copper alloy sheet material manufactured under specific manufacturing conditions. It has been found that high strength can be achieved in any direction of 0 °, 45 ° or 90 ° from the rolling direction to the vertical direction of rolling while having good conductivity. The present invention has been completed based on this finding.

That is, according to the present invention, the following means are provided.
(1) A total of 1.80 to 8.00% by mass of any one or two of Ni and Co, 0.40 to 2.00% by mass of Si , and further Sn 0.31% by mass or less, Zn 0.47 mass% or less, Ag 0.08 mass% or less, Mn 0.1 mass% or less, P 0.05 mass% or less, Mg 0.11 mass% or less, Cr 0.12 mass% or less, Fe 0.11 mass% or less, and Ti0 a range of .14 wt% or less, and the Sn, Zn, Ag, Mn, P, Mg, Cr, at least one element selected from the group consisting of F e, and Ti in a total from 0.000 to 2 .000% by mass, the balance is composed of copper and inevitable impurities, the electrical conductivity is 20 to 40% IACS or more, and 0 ° from the rolling direction (RD) to the rolling vertical direction (TD). Both the tensile strength in the direction of 45 ° and 90 ° It is a 020~1400MPa, copper alloy sheet.
(2) the Sn, Zn, Ag, Mn, P, Mg, Cr, the content of total of at least one element selected from the group consisting of F e, and Ti, with 0.005 to 2.000 wt% there (1) the copper alloy sheet according to item.
(3) A connector comprising the copper alloy sheet according to (1) or (2).
(4) The electrical conductivity is 20 to 40% IACS or more, and the tensile strength in the direction of 0 °, 45 °, and 90 ° from the rolling direction (RD) to the rolling vertical direction (TD) is 1020 to 1400 MPa. A method for producing a copper alloy sheet, comprising a total of 1.80 to 8.00 mass% of Ni or Co, or two or more of Ni and Co, 0.40 to 2.00 mass% of Si , and Sn 0.31 mass% or less, Zn 0.47 mass% or less, Ag 0.08 mass% or less, Mn 0.1 mass% or less, P 0.05 mass% or less, Mg 0.11 mass% or less, Cr 0.12 mass% or less, At least one element selected from the group consisting of Sn, Zn, Ag, Mn, P, Mg, Cr , Fe, and Ti, in a range of Fe 0.11% by mass or less and Ti 0.14% by mass or less. In total 0.000-2.0 A melting / casting step for melting and casting a copper alloy raw material containing 0% by mass and the balance consisting of copper and inevitable impurities, a homogenization heat treatment step for performing heat treatment at 900 to 1040 ° C. for 1 hour or more, and hot working The temperature range from the start to the end is 500 to 1040 ° C., the hot working step in which the working rate is 10 to 90%, the intermediate cold rolling step in which the working rate is 0 to 95%, and 300 to 430 ° C. A method for producing a copper alloy sheet, in which a heat treatment step for performing heat treatment for 5 minutes to 10 hours and a final cold rolling step with a processing rate of 60 to 99% are performed in this order.
(5) For the copper alloy used in the melting and casting process, Sn 0.31 mass% or less, Zn 0.47 mass% or less, Ag 0.08 mass% or less, Mn 0.1 mass% or less, P 0.05 mass% or less Mg 0.11 mass% or less, Cr 0.12 mass% or less, Fe 0.11 mass% or less, and Ti 0.14 mass% or less, and the Sn, Zn, Ag, Mn, P, Mg, Cr , The method for producing a copper alloy sheet according to the item (4), which contains in total 0.005 to 2.000 mass% of at least one element selected from the group consisting of Fe and Ti.
(6) The method for producing a copper alloy sheet according to (4) or (5), wherein after the final cold rolling step, strain relief annealing is performed at 200 to 500 ° C. for 5 seconds to 2 hours.

The copper alloy plate material of the present invention can be suitably used for a thin spring material for a camera module, a movable piece of a relay, etc., in addition to an external connection connector typified by a dock connector or a USB connector, due to its characteristics.
The copper alloy sheet of the present invention has a significantly higher strength than conventional ones in the direction of 0 °, 45 ° or 90 ° from the rolling direction to the vertical direction of rolling as the stress load direction to the spring. It can be used as a spring material that is difficult to deteriorate. For this reason, it is suitable as a connector material, for example.
Moreover, according to the manufacturing method of the copper alloy plate material of this invention, the copper alloy plate material which has the said outstanding characteristic can be manufactured suitably.

  The above and other features and advantages of the present invention will become more apparent from the following description, with reference where appropriate to the accompanying drawings.

FIG. 1 is a schematic diagram showing a relationship between a copper alloy sheet, a rolling direction (RD), a rolling vertical direction (TD), and a rolling surface vertical direction (ND). FIG. 2 is a schematic diagram showing test pieces in 0 °, 45 °, and 90 ° directions from the rolling direction to the vertical direction of rolling as test pieces in the tensile test and fatigue test. FIG. 3 is an explanatory diagram of local elongation. FIG. 3 shows a stress-strain curve in the 0 ° direction of Invention Example 205 as a representative example. The local elongation (e _L ) refers to the elongation until the test material breaks after the illustrated uniform elongation (e _U ). 4A is a {100} pole figure of the invention example 205, FIG. 4B is a comparative example 256, and FIG. 4C is a comparative example 257 by X-ray.

  A preferred embodiment of the copper alloy sheet material of the present invention will be described in detail. Here, the “copper alloy material” means a material obtained by processing a copper alloy material into a predetermined shape (for example, a plate, a strip, a foil, a bar, a wire, or the like). Among them, the term “plate material” refers to a material having a specific thickness and being stable in shape and having a spread in the plane direction. In a broad sense, it includes a strip material, a foil material, and a tube material in which the plate is tubular. .

  In FIG. 1, the relationship of the copper alloy sheet material 1 of this embodiment, and a rolling direction (RD), a rolling vertical direction (TD), and a rolling surface vertical direction (ND; Normal Direction) is shown. The rolling direction indicates a direction in which the plate material is rolled and stretched by a rolling roll or the like when the copper alloy plate material is manufactured. On the other hand, the rolling vertical direction is a direction perpendicular to the rolling direction and parallel to the rolling surface. The rolling surface vertical direction is a direction perpendicular to the rolling surface. Industrial copper alloy sheets are manufactured and shipped while being rolled. Therefore, immediately after the production of the copper alloy sheet, the longitudinal direction of the sheet is usually the rolling direction, and the width direction of the sheet is the vertical direction of rolling.

The copper alloy sheet of this embodiment contains one or two of Ni and Co and Si in specific amounts, and if necessary, Sn, Zn, Ag, Mn, P, Mg, Cr, Zr, Fe, and By containing a specific amount of at least one element selected from the group consisting of Ti and a specific alloy composition consisting of copper and inevitable impurities as the balance, the conductivity is 20 to 40% IACS or more, and the rolling direction The tensile strengths in the directions of 0 °, 45 °, and 90 ° from (RD) to the rolling vertical direction (TD) are all 1020 to 1400 MPa. Here, each of the three directions is a direction on a plane parallel to the rolling surface (that is, a surface formed in the rolling direction and the vertical direction of rolling). In FIG. 2, from the copper alloy sheet 1 of the present embodiment, the test piece 20 in the direction of 0 ° from the rolling direction (RD) to the vertical direction of rolling (TD), the test pieces 21 and 90 in the direction of 45 °. The manner in which the test pieces 22 in the direction of ° are sampled is indicated by dotted lines.
The copper alloy sheet material of the present embodiment is manufactured through a specific strong working process without performing a solution treatment, so that the processed structure is appropriately controlled to increase the strength, and from the rolling direction to the rolling vertical direction. In the direction of 0 °, 45 °, or 90 °, the strength is significantly higher than the conventional one.

  The Cu— (Ni, Co) —Si system used for the copper alloy sheet of the present embodiment is a precipitation hardening type alloy, and intermetallic compounds such as Ni—Si system, Co—Si system, and Ni—Co—Si system are the first. High strength can be obtained by precipitation hardening by dispersing as a two-phase in a copper matrix with a fine size of around several nanometers.

(Tensile strength: TS)
In the copper alloy sheet of this embodiment, the tensile strength in any direction of 0 °, 45 °, and 90 ° from the rolling direction to the vertical direction of rolling is 1020 MPa or more, preferably 1060 MPa or more. The upper limit of the tensile strength in any direction of 0 °, 45 °, and 90 ° from the rolling direction to the vertical direction of rolling is 1400 MPa or less, preferably 1350 MPa or less. If the tensile strength is within the above range, the fatigue resistance is also excellent. If the tensile strength is too low, the fatigue resistance is poor. On the other hand, if the tensile strength is too high, local elongation is difficult to occur. The tensile strength is JIS
Based on Z2241, stress (unit: MPa) with respect to the maximum force applied during the tensile test. Depending on the definition of σ _{TS in} FIG. 3, the stress at the point where the slope of the stress-strain curve is zero may be used as the tensile strength. On the other hand, in the present invention, it means that the tensile strength is set to a stress just before the inclination becomes zero.

(Conductivity: EC)
In the copper alloy sheet of the present embodiment, the conductivity is 20% IACS or more, preferably 23% IACS or more, and more preferably 26% IACS or more. If the conductivity is too high, the strength may decrease, so the upper limit is 40% IACS or less.

In the present embodiment, the above-mentioned “% IACS” represents the conductivity when the resistivity 1.7241 × 10 ⁻⁸ Ωm of universal standard annealed copper (International Annealed Copper Standard) is 100% IACS. It is.

(Crystal orientation control)
The crystal orientation distribution is controlled to improve the tensile strength and fatigue resistance in the 45 ° and 90 ° directions that are particularly noticeable in this embodiment. As shown in the {100} pole figure by X-rays representatively shown in FIG. 4, the copper alloy sheet material of the present embodiment (Invention Example 205, FIG. 4 (A)) uses the conventional manufacturing method (Comparative Example 256, FIG. 4). It can be seen that a crystal orientation distribution that was not seen in (B), Comparative Example 257, and FIG.

(Alloy composition)
Ni, Co, and Si are elements constituting the second phase. These form the intermetallic compound. These are essential additive elements of this embodiment. The total content of any one or two of Ni and Co is 1.80 to 8.00% by mass, preferably 2.40 to 5.00% by mass, more preferably 3.20 to 5%. 0.000% by mass. Moreover, content of Si is 0.40-2.00 mass%, Preferably it is 0.50-1.20 mass%, More preferably, it is 0.60-1.20 mass%. If the amount of these essential additive elements is too small, the effect obtained is insufficient, the strength is insufficient, and the fatigue resistance is also poor. On the other hand, if the amount of these essential additive elements is too large, the electrical conductivity may decrease. Alternatively, material cracks may occur during the rolling process. The conductivity is slightly better when Co is added, but rolling cracks are likely to occur depending on the conditions of hot rolling and cold rolling when the concentration of the essential additive element is high in the state containing Co. There is a case. Therefore, a more preferred embodiment of the present invention is one that does not contain Co in the second phase.

-Other elements The copper alloy sheet material of the present embodiment is at least one selected from the group consisting of Sn, Zn, Ag, Mn, P, Mg, Cr, Zr, Fe and Ti in addition to the essential additive elements. An element may be contained as an optional additive element. When the optional additive element is contained, the content of at least one element selected from the group consisting of Sn, Zn, Ag, Mn, P, Mg, Cr, Zr, Fe, and Ti is 0.005 in total. 2.000 mass%. The optional additive element has an effect of promoting the refinement of crystal grains and improving the strength characteristics and fatigue characteristics in intermediate cold rolling [Step 5] and final cold rolling [Step 7] described later. In addition, it has an effect of improving the stress relaxation resistance, and is suitable when the use environment is a high temperature such as 100 ° C. or higher. However, if the content of these optional additive elements is too large, there is a case in which the adverse effect of lowering the electrical conductivity is caused or material cracking may occur during the rolling process.

-Inevitable impurities Inevitable impurities in copper alloys are ordinary elements contained in copper alloys. Examples of inevitable impurities include O, H, S, Pb, As, Cd, and Sb. These are allowed to contain up to about 0.1% by mass as the total amount.

(Production method)
As a conventional method, in a conventional method for producing a precipitation hardening copper alloy material, after making it into a supersaturated solid solution state by solution heat treatment, it is precipitated by aging treatment, and temper rolling (finish rolling) and temper annealing as necessary (Low temperature annealing, strain relief annealing) is performed. The manufacturing methods F, J, K, and L of comparative examples described later correspond to this.

  On the other hand, in the present invention, a process different from the conventional method is effective. For example, the following process is effective. However, the present invention is not limited to the following method.

  An example of a method for producing a copper alloy sheet according to the present embodiment is to obtain an ingot by melting / casting [Step 1], and to this ingot, hot processing such as homogenization heat treatment [Step 2], hot rolling, etc. [Step 3], water cooling [Step 4], intermediate cold rolling [Step 5], heat treatment for aging precipitation [Step 6], final cold rolling [Step 7], strain relief annealing [Step 8] in this order. The method of performing is mentioned. The strain relief annealing [Step 8] may be omitted if predetermined physical properties are obtained.

  In this embodiment, the combination of a series of the above processes and the condition of the intermediate cold rolling [Step 5] is a processing rate of 0 to 95%, and the condition of the aging treatment [Step 6] is 300 to 430 ° C. for 5 minutes. 10 hours and the processing rate of the final cold rolling [Step 7] is 60 to 99%, which is achieved by limiting the combination of specific conditions in each step. The mechanism here is estimated as follows. The action of the (Ni, Co) -Si compound precipitated in the aging treatment [Step 6] changes the dislocation distribution state and crystal rotation in the subsequent final cold rolling [Step 7]. Then, by taking a high rolling ratio in the final cold rolling [Step 7], the crystal grains in the final cold rolling [Step 7] are divided.

The preferable heat treatment and processing conditions in each step are as follows.
The homogenization heat treatment [Step 2] is held at 900 to 1040 ° C. for 1 hour or longer, preferably 5 to 10 hours.
In the hot working [Step 3] such as hot rolling, the temperature range from the start to the end of hot working is 500 to 1040 ° C., and the working rate is 10 to 90%.
In the water cooling [Step 4], the cooling rate is usually 1 to 200 ° C./second.
The intermediate cold rolling [Step 5] has a processing rate of 0 to 95%, preferably 71 to 95%.
The aging treatment [Step 6] is also referred to as aging precipitation treatment, and the condition is holding at 300 to 430 ° C. for 5 minutes to 10 hours, and a preferable temperature range is 330 to 360 ° C.
The final cold rolling [Step 7] has a processing rate of 60 to 99%, preferably 60 to 89%.
The strain relief annealing [Step 8] is held at 200 to 500 ° C. for 5 seconds to 2 hours. If the holding time is too long, the strength decreases, and therefore it is preferable to perform short-time annealing for 5 seconds or more and 5 minutes or less.

Here, the processing rate (or cross-sectional reduction rate in rolling) is a value defined by the following equation.
Processing rate (%) = {(t ₁ −t ₂ ) / t ₁ } × 100
In the formula, t ₁ represents the thickness before rolling, and t ₂ represents the thickness after rolling.

  In addition, after each heat treatment or rolling, the surface oxide layer may be removed by chamfering, acid cleaning, or surface polishing, if necessary, depending on the state of oxidation or roughness of the material surface. Further, depending on the shape, correction by a tension leveler may be performed as necessary. Also, when the surface roughness of the material is large due to transfer of unevenness of the rolling roll or oil pits, the rolling speed, rolling oil, diameter of the rolling roll, surface roughness of the rolling roll, reduction amount of one pass during rolling, etc. The rolling conditions can be adjusted.

(Thickness)
The copper alloy sheet material of this embodiment has a final sheet thickness of 30 μm to 1 mm after finish rolling. Preferably, it is 40 micrometers-0.3 mm.

(Physical properties)
The copper alloy sheet material of this embodiment preferably has the following physical properties.

(Fatigue resistance)
In one preferred embodiment of the copper alloy sheet according to the present embodiment, in a fatigue test specified by JIS Z 2273, fatigue resistance in any direction of 0 °, 45 °, and 90 ° from the rolling direction to the vertical direction of rolling. Excellent characteristics. Specifically, when the test piece is repeatedly bent at a load stress of 500 MPa, the number of times until it breaks is preferably 4 × 10 ⁴ times or more. This is the number of times corresponding to 10 insertions / removals every day for 10 years. More preferably, it is 8 × 10 ⁴ times or more, and further preferably 11 × 10 ⁴ times or more. Depending on the terminal design, the load stress in the 90 ° direction is particularly high, so that particularly good fatigue characteristics may be required. As a more preferred embodiment of the present invention, the 90 ° life is 2 × 10 ⁵ times or more.

(Local growth)
In one preferable embodiment of the copper alloy sheet according to the present invention, the local elongation is preferably 0.03 to 10%, more preferably 0.08 to 10%, and further preferably 0.15 to 10%.
In the tensile test, if the maximum load (tensile strength σ _TS ) is exceeded, necking occurs in a part of the test piece. This elongation after the occurrence of constriction is called local elongation. In FIG. 3, the stress-strain curve in 0 degree direction of the invention example 205 is shown as a typical example. e _U corresponds to uniform elongation, and e _L corresponds to local elongation. In general, it is difficult to achieve local elongation as the strength of the material is increased. The copper alloy sheet material of the present invention preferably has a constant local elongation while having a high strength.

  Hereinafter, the present invention will be described in more detail based on examples, but the present invention is not limited thereto.

(Example 1)
An alloy raw material containing the alloy constituent elements shown in Table 1 and the balance consisting of Cu and inevitable impurities was melted in a high-frequency melting furnace and cast to obtain an ingot. And the test material of the copper alloy board | plate material of the comparative example was manufactured separately by the manufacturing method in any one of following A, B, C, D, E, and F separately from the invention example according to this invention. Table 1 shows which of A, B, C, D, E, and F was used. The final thickness of the copper alloy sheet was 0.1 mm. This final plate thickness is the same in the production methods J, K, and L described below unless otherwise specified.
The numbers underlined in the table mean that the alloy component content or manufacturing method specified in the present invention was not satisfied, or that the physical properties did not satisfy the range specified in the present invention or the preferred range. To do.

(Manufacturing method A)
The ingot was subjected to a homogenization heat treatment that was held at 900 to 1040 ° C. for 1 hour or more and 10 hours or less, and hot rolling was performed in this high temperature state. The end temperature of hot rolling was 500 ° C. or higher, and the processing rate was 10 to 90%. After the hot rolling was finished, it was cooled with water. Thereafter, it was chamfered as necessary. Thereafter, intermediate cold rolling with a processing rate of 0 to 95%, aging treatment at 300 to 430 ° C. for 5 minutes to 10 hours, final cold rolling with a processing rate of 60 to 99%, and the following strain relief annealing are performed. I went in order.

(Manufacturing method B)
It carried out similarly to the said manufacturing method A except having made the processing rate of the said last cold rolling into 99.1 to 99.9%.

(Manufacturing method C)
It carried out similarly to the said manufacturing method A except having made the processing rate of the said last cold rolling into 30 to 59%.

(Manufacturing method D)
It was carried out in the same manner as in Production Method A except that the heating temperature for the aging treatment was 250 to 290 ° C. and the processing rate of the final cold rolling was 60 to 89%.

(Manufacturing method E)
It carried out similarly to the said manufacturing method A except having set the heating temperature of the said aging treatment to 440-500 degreeC, and having set the processing rate of the said last cold rolling to 60 to 89%.

(Production method F)
After the intermediate cold rolling and before the aging treatment, a solution treatment is performed in which water quenching is performed at 700 to 1000 ° C. for 5 seconds to 10 minutes, and the processing rate of the final cold rolling is set to 60 to The procedure was the same as in Production Method A except that the content was 89%.

The conditions for strain relief annealing in the production methods A, B, C, D, E, and F were held at 200 to 500 ° C. for 5 seconds to 5 minutes.
After each heat treatment and rolling, the surface oxide layer was removed by chamfering, acid cleaning, or surface polishing, if necessary, depending on the state of oxidation and roughness of the material surface. Further, according to the shape, correction with a tension leveler was performed as necessary. In addition, when the roughness of the material surface is large due to transfer of unevenness of the rolling roll or oil pits, the rolling speed, rolling oil, diameter of the rolling roll, surface roughness of the rolling roll, reduction amount of one pass during rolling, etc. The rolling conditions were adjusted.

  In addition, as another comparative example, a prototype of a copper alloy sheet material was obtained by trial manufacture by any of the following production methods J, K, and L. The conditions of the manufacturing methods J, K, and L followed those of the manufacturing methods described in each patent document.

(Production method J) Patent document 6: Production method of Example 2 of JP-A-2008-095186 A raw material providing the copper alloy composition shown in Table 1 below was melted in a high-frequency melting furnace, and this was DC (direct casting). The ingot was cast into an ingot having a thickness of 30 mm, a width of 100 mm, and a length of 150 mm by the method, and the obtained ingot was kept at a temperature of 1000 ° C. for 1 hour, and then hot-rolled to a thickness of 12 mm and quickly cooled. Next, both sides of the hot-rolled plate are cut 1.5 mm each to remove the oxide film, then cold-rolled to a thickness of 0.15 to 0.1 mm, and then at a temperature range of 825 to 925 ° C. for 15 seconds. Solution treatment was performed, and immediately thereafter, cooling was performed at a cooling rate of 10 ° C./second or more. Next, aging heat treatment was performed at 420 to 480 ° C. for 1 to 3 hours, and then immediately cooled at a cooling rate of about 1 to 10 ° C./second.
Subsequently, it cold-rolled with the rolling rate of 30% or less, and finished it into the board | plate material with a board thickness of 0.1 mm. The conditions for solution treatment and aging heat treatment were appropriately selected according to the alloy composition. After cold rolling, strain relief annealing was performed at 650 ° C. for 3 seconds.

(Manufacturing method K) Patent document 7: Example 1 described in Japanese Patent Application Laid-Open No. 2012-246549, manufacturing method of step A A raw material giving the copper alloy composition shown in Table 1 below was melted in a high-frequency melting furnace, and this was cast. The ingot was obtained. Using this state as a providing material, a test material for a copper alloy sheet was manufactured in the following steps. The final alloy sheet thickness was 0.12 mm.
Perform homogenization heat treatment at a temperature of 950 to 1050 ° C. for 3 minutes to 10 hours, perform hot rolling at 500 to 950 ° C., and then perform heat treatment at 400 to 800 ° C. for 5 seconds to 20 hours to remove oxide scale. For this reason, the surface was cut. Thereafter, cold rolling 1 with a processing rate of 90 to 99% was performed, intermediate annealing was performed at a temperature of 400 to 700 ° C. for 5 seconds to 20 hours, and cold rolling 2 with a processing rate of 3 to 80% was performed. . Thereafter, a solution heat treatment is performed at a temperature of 800 to 950 ° C. for 5 seconds to 50 seconds, an aging precipitation heat treatment is performed at a temperature of 350 to 600 ° C. for 5 minutes to 20 hours, and a finish rolling of 5 to 50% is performed. And temper annealing was performed at a temperature of 300 to 700 ° C. for 10 seconds to 20 hours.

(Manufacturing Method L) Patent Document 3: Manufacturing Method of Invention Example 1 described in Japanese Patent Application Laid-Open No. 2006-152392 Copper that gives a copper alloy composition (Cu-6.0Ni-1.2Si-0.02P) shown in Table 1 below The alloy was cast to produce a copper alloy plate. As other elements (inevitable impurity elements) other than those described above, Al, Fe, Ti, Be, V, Nb, Mo, and W were 0.5% by mass or less in total. Further, the total amount of elements such as B, C, Na, S, Ca, As, Se, Cd, In, Sb, Pb, Bi, and MM (Misch metal) was 0.1% by mass or less.
As a specific method for producing a copper alloy plate, a kryptor furnace is melted under a charcoal coating in the atmosphere, cast into a cast iron book mold, and an ingot having a thickness of 50 mm, a width of 75 mm, and a length of 180 mm is obtained. Obtained. Then, after chamfering the surface of the ingot, it was hot-rolled at a temperature of 950 ° C. until the thickness became 15 mm, and rapidly cooled into water from a temperature of 750 ° C. or higher. Next, after removing the oxide scale, cold rolling was performed to obtain a plate having a thickness of 0.75 mm.
Subsequently, after performing a solution treatment by heating for 20 seconds at a temperature of 900 ° C. using a salt bath furnace, after quenching in water, the finish cold rolling of the latter half with a processing rate of 20%, a thickness of 0.6 mm Cold rolled. This cold-rolled sheet was subjected to an aging treatment at a temperature of 450 ° C. for 4 hours.

  About the test material of the invention example according to this invention and a comparative example, each characteristic was measured and evaluated as follows. The results are also shown in Table 1.

a. Tensile strength: TS
A test piece of JIS Z2201-13B cut out at 0 ° (rolling direction), 45 ° or 90 ° (rolling vertical direction) from the rolling direction to the rolling vertical direction as shown in FIG. 2 in accordance with JIS Z2241. Then, three samples were measured in each direction, and the average value was shown. The tensile strength was a stress (unit: MPa) with respect to the maximum force applied during the tensile test.

b. Conductivity: EC
About each test material, the specific resistance was measured by the four probe method in the thermostat kept at 20 degreeC (+/- 0.5 degreeC), and the electrical conductivity was computed. In addition, the distance between terminals was 100 mm.

c. As shown in FIG. 2, a test piece of JIS Z2201-13B cut out at 0 ° (rolling direction), 45 ° or 90 ° (rolling vertical direction) from the rolling direction to the rolling vertical direction, According to JIS Z 2273, three times in each direction, the number of repetitions until breakage was measured when repeated bending was performed at a load stress of 500 MPa, and the average value was shown.

d. Local growth: e _L
As shown in FIG. 3, the local elongation (e _L ) was determined in the same tensile test as described above.

  As shown in Table 1, Invention Examples 101 to 110 that satisfy the definition of the present invention were all excellent in all characteristics. That is, in the inventive examples 101 to 110, the higher the Ni / Co and Si concentrations are within a predetermined range, the higher the tensile strength in any of the 0 °, 45 °, and 90 ° directions from the rolling direction to the vertical direction of rolling [ TS] and fatigue resistance (number of repetitions) are shown. Moreover, each invention example had local elongation except for the 0 ° or 90 ° direction from the rolling direction of Invention Examples 104 and 106 toward the vertical direction of rolling.

On the other hand, in each comparative example, either one of the alloy composition and the production condition did not satisfy the condition defined in the present invention, and therefore, either 0 °, 45 ° or 90 ° direction from the rolling direction to the vertical direction of rolling. , The tensile strength [TS] was low without satisfying the conditions defined in the present invention.
More specifically, in Comparative Example 151, since Ni / Co and Si were too little, the condition that the tensile strength [TS] is defined in the present invention in the 0 ° or 45 ° direction from the rolling direction to the rolling vertical direction. It was low without meeting. Further, Comparative Example 151 was inferior in fatigue resistance characteristics (number of repetitions) in the 0 ° or 45 ° direction from the rolling direction to the rolling vertical direction. In Comparative Example 152 in which the contents of Ni and Si were too large, rolling cracks occurred and productivity was inferior. In Comparative Examples 153 to 156 according to the production methods C, D, E, or F, the manufacturing conditions deviate from the conditions defined in the present invention, and in either the 0 °, 45 °, or 90 ° direction from the rolling direction to the vertical direction of rolling. The tensile strength [TS] was low without satisfying the conditions defined in the present invention. Moreover, Comparative Examples 153 to 156 were inferior in fatigue resistance characteristics (repetition count) in any of 0 °, 45 °, and 90 ° directions from the rolling direction to the vertical direction of rolling.

  As other comparative examples, the comparative example 157 by the manufacturing method J and the comparative example 158 by the manufacturing method K are both 0 °, 45 ° from the rolling direction to the vertical direction of the rolling, and the manufacturing conditions deviate from the conditions defined in the present invention. In any of the 90 ° directions, the tensile strength [TS] was low without satisfying the conditions defined in the present invention. Further, the fatigue resistance was inferior in any of 0 °, 45 ° and 90 ° directions from the rolling direction to the vertical direction of rolling.

(Example 2)
By the same manufacturing method and test / measurement method as in Example 1, copper alloy sheet materials were manufactured using various copper alloys shown in Table 2, and their characteristics were evaluated. The results are shown in Table 2.

  As shown in Table 2, Invention Examples 201 to 210 that satisfy the provisions of the present invention were all excellent in all characteristics. Higher tensile strength [TS] and fatigue resistance in any of 0 °, 45 °, or 90 ° direction from the rolling direction to the vertical direction of rolling, although not in all the test examples, due to the additive effect of the optional additive element A tendency to improve (the number of repetitions) was observed. Moreover, each invention example had local elongation except for the 0 ° or 90 ° direction from the rolling direction of Invention Examples 203 and 206 toward the vertical direction of rolling.

On the other hand, in each comparative example, either one of the alloy composition and the production condition did not satisfy the condition defined in the present invention, and therefore, either 0 °, 45 ° or 90 ° direction from the rolling direction to the vertical direction of rolling. , The tensile strength [TS] was low without satisfying the conditions defined in the present invention.
More specifically, in Comparative Example 251 in which the auxiliary additive element (Sn in this example) was too much, a rolling crack occurred and the productivity was inferior. In Comparative Examples 252 to 255 according to the production methods C, D, E, or F, the manufacturing conditions deviate from the conditions defined in the present invention, and in either the 0 °, 45 °, or 90 ° direction from the rolling direction to the vertical direction of rolling. The tensile strength [TS] was low without satisfying the conditions defined in the present invention. Further, Comparative Examples 252 to 255 were inferior in fatigue resistance in any of 0 °, 45 °, and 90 ° directions from the rolling direction to the rolling vertical direction.

  As other comparative examples, the comparative example 256 by the manufacturing method J, the comparative example 257 by the manufacturing method K, and the comparative example 258 by the manufacturing method L are all out of the conditions defined in the present invention by the manufacturing conditions, and are directed from the rolling direction to the rolling vertical direction. The tensile strength [TS] was low without satisfying the conditions defined in the present invention in any of the 0 °, 45 °, and 90 ° directions. Further, the fatigue resistance was inferior in any of 0 °, 45 ° and 90 ° directions from the rolling direction to the vertical direction of rolling.

  As long as the copper alloy plate material of the present invention is a connector, any type can be suitably used. In particular, it can be suitably used as an external connection connector represented by a dock connector or a USB connector, a thin spring material for a camera module, or a movable piece of a relay.

  While the invention has been described in conjunction with the embodiments thereof, it is not intended that the invention be limited in any detail to the description unless otherwise specified, which is contrary to the spirit and scope of the invention as set forth in the appended claims. I think it should be interpreted widely.

DESCRIPTION OF SYMBOLS 1 Copper alloy board | plate material 20 The test piece for measuring the tensile strength and fatigue resistance of a 0 degree direction from a rolling direction (RD) to a rolling vertical direction (TD) 21 Rolling direction (RD) to rolling vertical direction (TD) Specimen for Measuring Tensile Strength and Fatigue Resistance in 45 ° direction toward 22 To measure Tensile Strength and Fatigue Resistance in 90 ° direction from rolling direction (RD) to vertical direction of rolling (TD) Specimen

Claims (6)

It contains 1.80 to 8.00 mass% in total of any one or two of Ni and Co, 0.40 to 2.00 mass% of Si , and further Sn 0.31 mass% or less, Zn 1.85 Mass% or less, Ag 0.08 mass% or less, Mn 0.1 mass% or less, P 0.05 mass% or less, Mg 0.11 mass% or less, Cr 0.12 mass% or less, Fe 0.11 mass% or less, and Ti 0.14 mass% % , And a total of at least one element selected from the group consisting of Sn, Zn, Ag, Mn, P, Mg, Cr 2 , Fe and Ti is 0.000 to 2.000 mass Containing, and the balance has a composition consisting of copper and inevitable impurities,
Conductivity is 20-40% IACS or more,
A copper alloy sheet having a tensile strength of 1020 to 1400 MPa in the direction of 0 °, 45 °, and 90 ° from the rolling direction (RD) to the rolling vertical direction (TD). The Sn, Zn, Ag, Mn, P, Mg, Cr, the content of total of at least one element selected from the group consisting of F e, and Ti, claims a 0.005 to 2.000 wt% The copper alloy sheet material according to 1.   The connector which consists of a copper alloy board | plate material of Claim 1 or 2. Copper alloy having an electrical conductivity of 20 to 40% IACS or more and tensile strengths in the directions of 0 °, 45 °, and 90 ° from the rolling direction (RD) to the vertical direction of rolling (TD) are 1020 to 1400 MPa. It is a manufacturing method of a board | plate material , Comprising: One or two types of Ni and Co are contained in a total of 1.80-8.00 mass%, Si is 0.40-2.00 mass% , Furthermore, Sn0. 31 mass% or less, Zn 1.85 mass% or less, Ag 0.08 mass% or less, Mn 0.1 mass% or less, P0.05 mass% or less, Mg0.11 mass% or less, Cr0.12 mass% or less, Fe0.11 A total of at least one element selected from the group consisting of Sn, Zn, Ag, Mn, P, Mg, Cr , Fe and Ti, in a range of not more than mass% and not more than 0.14 mass% of Ti. 0.000 to 2.000 quality % And containing a melting and casting process the balance to dissolve the raw material of the copper alloy consisting of copper and unavoidable impurities casting,
A homogenization heat treatment step of performing heat treatment at 900 to 1040 ° C. for 1 hour or more;
A hot working step in which the temperature range from the start to the end of hot working is 500 to 1040 ° C., and the working rate is 10 to 90%;
An intermediate cold rolling step with a processing rate of 0 to 95%;
A heat treatment step of performing heat treatment at 300 to 430 ° C. for 5 minutes to 10 hours;
A final cold rolling step with a processing rate of 60-99%;
A method for producing a copper alloy sheet material in this order. The copper alloy to be used for the melting / casting step is Sn 0.31 mass% or less, Zn 1.85 mass% or less, Ag 0.08 mass% or less, Mn 0.1 mass% or less, P 0.05 mass% or less, Mg 0. 11 mass% or less, Cr 0.12 mass% or less, Fe 0.11 mass% or less and Ti 0.14 mass% or less, and the Sn, Zn, Ag, Mn, P, Mg, Cr 2 , Fe and The manufacturing method of the copper alloy board | plate material of Claim 4 which contains 0.005-1.000 mass% of at least 1 sort (s) of elements chosen from the group which consists of Ti in total. The method for producing a copper alloy sheet according to claim 4 or 5, wherein after the final cold rolling step, strain relief annealing is performed at 200 to 500 ° C for 5 seconds to 2 hours.

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